CA1084734A - Ductile ferritic steels - Google Patents
Ductile ferritic steelsInfo
- Publication number
- CA1084734A CA1084734A CA279,345A CA279345A CA1084734A CA 1084734 A CA1084734 A CA 1084734A CA 279345 A CA279345 A CA 279345A CA 1084734 A CA1084734 A CA 1084734A
- Authority
- CA
- Canada
- Prior art keywords
- content
- contents
- steel
- chromium
- steels
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Arc Welding In General (AREA)
- Organic Low-Molecular-Weight Compounds And Preparation Thereof (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Catalysts (AREA)
- Meat, Egg Or Seafood Products (AREA)
Abstract
ABSTRACT OF THE DISCLOSURE
Ferritic, stabilised, stainless and corrosion-resistant chromium-molybdenum steels with a carbon content of from 0.01 to 0.025%, a nitrogen content of from 0.005 to 0.025%, a chromium content of from 20.0 to 30.0%, a molybdenum content of from 3.0 to 5.0%, manganese and silicon contents of from 0.02 to 1.0% in each case and vanadium, tungsten, cobalt and aluminum contents of at most 0.25% in each case and also with a nickel content of from 3.2 to 4.8%, a copper content of from 0.1 to 1.0%, a titanium content of from 0.2 to 0.7% and/or a niobium content of from 0.2 to 1.0%, the rest being iron with the usual impurities, alloying additions of boron and/or zirconium being permitted in quantities which correspond to the prior art. Such stabilised, ferritic, chromium-molybdenum steels have low transition temperatures reducing the likelihood of their becoming brittle upon welding.
Ferritic, stabilised, stainless and corrosion-resistant chromium-molybdenum steels with a carbon content of from 0.01 to 0.025%, a nitrogen content of from 0.005 to 0.025%, a chromium content of from 20.0 to 30.0%, a molybdenum content of from 3.0 to 5.0%, manganese and silicon contents of from 0.02 to 1.0% in each case and vanadium, tungsten, cobalt and aluminum contents of at most 0.25% in each case and also with a nickel content of from 3.2 to 4.8%, a copper content of from 0.1 to 1.0%, a titanium content of from 0.2 to 0.7% and/or a niobium content of from 0.2 to 1.0%, the rest being iron with the usual impurities, alloying additions of boron and/or zirconium being permitted in quantities which correspond to the prior art. Such stabilised, ferritic, chromium-molybdenum steels have low transition temperatures reducing the likelihood of their becoming brittle upon welding.
Description
~ 3 4 In recent years, ferritic chromium molybdenum steels have been the subject of exhaustive investigations in order to ascertain the essence and structural relationship of the deficiencies attending these steels in relation to austenitic Cr-Ni steels so that they may be minimised or eliminated which is of particular economic significance in view of the advantages which these steels have over the austenitic steels among others. Above all, the knowlsdge of the influence of the inclusion elements carbon and nitrogen has led to new metallurgical processes by which the contents of these elements can be reduced to below the hitherto usual levels. However~ this involves the use of metallurgical techniques and installations which use up a large part of the desired economy. AlsoJ the results obtained ha~e been unsatisfactory, p~rticularly in regard to the position of the transition temperature, i.e. the temperature at which the steel changes abruptly from the ductile state to the brittle state.
The use of stabilising elements for fixing the C- and N2-contents~at the low contents of these elements of less than 0.03% led to additions which, for Ti for example, no longer correspond to the stoichiometry o~
1:4, but instead had to be increased to 1:15 which gave contents that adversely affected the property values of the steels. In general, C and N~ contents below 0.015%
are now proposed, Si contents of 0-3%, manganese contents of 0-1%, nickel contents of 0-5% and copper contents of 0-2% being permitted in certain cases because no influence .
on the properties of these steels was associated with -these elements in the ranges indicated, as is apparent from ~ -the mere fact tha~ these elements need not be present.
~ .
The use of stabilising elements for fixing the C- and N2-contents~at the low contents of these elements of less than 0.03% led to additions which, for Ti for example, no longer correspond to the stoichiometry o~
1:4, but instead had to be increased to 1:15 which gave contents that adversely affected the property values of the steels. In general, C and N~ contents below 0.015%
are now proposed, Si contents of 0-3%, manganese contents of 0-1%, nickel contents of 0-5% and copper contents of 0-2% being permitted in certain cases because no influence .
on the properties of these steels was associated with -these elements in the ranges indicated, as is apparent from ~ -the mere fact tha~ these elements need not be present.
~ .
-2- ~
~...... ..... ; , ~
~...... ..... ; , ~
3~73 4 The position of the transition temperature is particularly in~oTtant for weldin~ which is of course necessary in thoso cases where *hese steels are used for the manufacture of industrial products The above-mentioned steels which, in the unwelded state, show ductility values o an acceptable nature ~ecome ~rittle in the weld seam and in the zones adjacent the weld seam.
Investigations which fox~ the basis of the present invention have now produced the suprising and unexpected result that stabilised ferritic chromium-molybdenum steels can have transition temperatures far below room temperature, particularly in the weld seam and in the zones directly adjacent the ~eld seam, providing the steels known per se have added to them quantities o nickel and copper which lie within a certain limited range, the C and N2 ~ :
contents also being kept within a certain percentage range which surpTisingly ~ .
lies at relatively high contents, and finally quantities of Ti or Nb which are below the usual equivalents, but amount to at least 0,2~, in addition to ;`
~hich the Ti content may amount to 4 times the ~C+N2~-content and the Nb content to 8 times the (C+N2)~content, their maximum levels amounting to 0~7~ and 1~0%9 respectively.
Accordingly, the.present invention provides ferritic, stabilised, stainless and corrosion-resistant chromium molybdenum steels with, expressed : :
; 20 in weight percent, a carbon content of from 0.01 to 0.025~, a nitrogencontent of f~om 0.005 to 0.025~, a chromium content of from 20.0 to 30.0%J
a molybdenum content of ~rom 3.0 to 5.0%, mangan~so and silicon contents of ~ .
P~om 0,02 to 1~0~ in each cnse and vanadium, tungsten) cobalt and aluminium contents o~ at most 0~25~ in each case, characterised in that they addition- ~.
ally contain nickel in a quantity of fTom 3.2 to 4.8%, copper in a quantity ~.
of E~om 0.1 to 1,0~, titanium in a quantity of from 0.2 to 0.7% and/or nio~ium iTI a quantity of from 0,2 to 1.0%j the rest consisting of iron with .-~he usual impurities, alloying additions of boron and/or zirconium being permitted in quantities which correspond to the prior art.
The ~emarkable and completely unexpected feature of the invention . ;
is that, for relatively high (C~N2~- contents, preferably from 0~15~ to 0~04%, relatively large amounts of nickel and, to a lesser extent, of 3_ ' 73~
copper have to be added to obtain high ductility values coupled wit.h th0 same high resistance to corrosion at room temperature and at te~peratures below Toom temp~rature, particularly in th~ welding zone.
~ or example, for chromium contents o from 22.0 to 24.0~ and moly~denum contents of f~om 3.5 to 4.5%, the nickel cont~nt preferably amounts to between 3,5 and 4.2~. Fo~ chromium contents of ~rom 27.0 ~o 3Q.0% and Mo contents of from 3.7 to 4.2%, the nickel content amounts to between 3.9 and 4.5%.
A preferred composition for a ferritic, stabilised, ch~omium-lQ molybdenum steel includes, by weight p~rcent:
c n. 012~Q,025%
si 0.02 a~s%
Mn ~02~0.5%
c~ 2a.0~22.0%
Ni 3.2_3.5%
Mo 3,a-4,5%
Cu Q~2~0,5%
Ti 0.,2 ~ 4x(C~N2~, but at most Q,7% and/or Nb 0.2 ~ 8x(C~N2), but at most 1.0%
N2 0~005 to 0.015%.
Another pr~ferred composition for a erTitic, stabilised, chromium~ :
moly~denum steel includes, by weight percent:
C 0.012 0.025%
Si 0.02 0,5%
Mn 0~02~0.5%
Cr 24,5~27,0%
Ni 3.5~4~2%
Mo 3,7-4~5~
Cu Q,2~0,S%
30. Ti Q,2 ~ 4x(C~N2~, but at most 0.7% or Nb 0,4 ~ 8x~C~N21, but at most 1~0%
N2 a~o~s.Q~ols%, 3~ :
.
73~ 1 .
In order to demonstrate the surprising and unexpected effect of adding nickel in par~icular to ferrlti~ Cr-Mo steels, the duetillty values determined by notched impact tests are reported in the following with reference to two Examples using steels with the preferred composition according to the invention and, for comparison, conventional steels.
Steels A and C have the composition according to the invention.
EXAMPLE I EXAMPLE II
Steel A Steel B Steel C Steel D ~ ;
C 0.012 0.011 0.014 0.012 `~ `
Si 0.4 0.35 0.41 0.32 Mn 0.32 0.28 0.39 0.33 ; `
Cr 25.7 25.3 21.1 21.2 Ni 4.20 0.10 3.5 0.4 Mo 4.08 3.1 3.2 3.1 `
Ti 0.45 0.41 0.39 0.35 ~-Cu 0.55 0.010 0.38 0.45 Al 0.059 0.049 0.048 0.05 Nb 0.011 0.021 N2 0.015 0.010 0.010 0.0~0 The ductillty v~lues of steels A, B, C and D are shown ~n the orm of graphs ln Figures 1, 2~ 3 and 4, respectively.
The curves "GM" relate to the base material whilst the curves ~'SZ" relate to the zones ad~acent the weld seam which are particularly exposed to the influence of the welding temperature in tenms of embrittlement.
Comparison of the curves "GM" of the two steels A and B shows that the trsn ition temperature of the ~:, steel A according to the invention lie~ between -60~C
and -80C whereas the conventional steel B has a transitio~ temperature which lies between +80C and +100~C.
Comparison of the curves "5Z" shows a transition temperature for the steel A according to the invention of from -40C to -20C and, for the comparison steel B, a transition temperature of from +120~C to ~140C.
The curve "GM" for steel C shows a transition temperature in the range from -30C to -50C. For steel D9 the characteristic values are in the ra~ge from +10C to ~ -+30C. Comparison of ~he curves "SZ" shows a transition temperature for steel C according to the invention of from -10C to + 0C and, for the comparison steel D~ a transition temperature o~ from ~40C to ~50C
So far as the expert is concerned, these results ~ .show that steels, particularly sheet steels, according :~
to the invention in welded constructions do not become `-brittle at room temperature or at temperatures below room temperature. ~ ~ -It is also clear to the expert that the additions of nickel and copper have t~ be selected in such a way that, for optimum ductility, there is little or no reduction in the resistance to stress-corrosion which would be the case for example if additions above th`e upper limits ~or Ni and Cu according to the~invention were to be made, for example 5.0% for Ni and 2.0% for Cu.
The necessary de8ree of invention is embodied in the specified limits of the various alloying ranges, : :
particularly for Ni and Cu. ~:;
So far as the C~N2-content is concerned, it is pointed out that the content ~prescribed in accordance with the invention, namely a relatively high (C~N2)-content , . ~ .
;::
,`-. :
~ 0 ~ 47 3 4 guarantee the reproducibility of the steels which is not the case when the (C~N2)-content is less than 0.015%
and when the objective is for the sum of (C+N2) not to exceed 0~01%~ In addition, reproducibility i~
, facilitated by the nickel content according-to the ;~
invention whereby even fairly large fluctuatiDns in the ~ -C~N2 content have no effect upon the ductility of the steel.
~ ,.
~';
:' .' ' '. ',' .
- ' ~ .
, . ' , ' ~:
` ~ :
` ~
-6- ::
. . .
.
, ~..... .. . .. . . .
Investigations which fox~ the basis of the present invention have now produced the suprising and unexpected result that stabilised ferritic chromium-molybdenum steels can have transition temperatures far below room temperature, particularly in the weld seam and in the zones directly adjacent the ~eld seam, providing the steels known per se have added to them quantities o nickel and copper which lie within a certain limited range, the C and N2 ~ :
contents also being kept within a certain percentage range which surpTisingly ~ .
lies at relatively high contents, and finally quantities of Ti or Nb which are below the usual equivalents, but amount to at least 0,2~, in addition to ;`
~hich the Ti content may amount to 4 times the ~C+N2~-content and the Nb content to 8 times the (C+N2)~content, their maximum levels amounting to 0~7~ and 1~0%9 respectively.
Accordingly, the.present invention provides ferritic, stabilised, stainless and corrosion-resistant chromium molybdenum steels with, expressed : :
; 20 in weight percent, a carbon content of from 0.01 to 0.025~, a nitrogencontent of f~om 0.005 to 0.025~, a chromium content of from 20.0 to 30.0%J
a molybdenum content of ~rom 3.0 to 5.0%, mangan~so and silicon contents of ~ .
P~om 0,02 to 1~0~ in each cnse and vanadium, tungsten) cobalt and aluminium contents o~ at most 0~25~ in each case, characterised in that they addition- ~.
ally contain nickel in a quantity of fTom 3.2 to 4.8%, copper in a quantity ~.
of E~om 0.1 to 1,0~, titanium in a quantity of from 0.2 to 0.7% and/or nio~ium iTI a quantity of from 0,2 to 1.0%j the rest consisting of iron with .-~he usual impurities, alloying additions of boron and/or zirconium being permitted in quantities which correspond to the prior art.
The ~emarkable and completely unexpected feature of the invention . ;
is that, for relatively high (C~N2~- contents, preferably from 0~15~ to 0~04%, relatively large amounts of nickel and, to a lesser extent, of 3_ ' 73~
copper have to be added to obtain high ductility values coupled wit.h th0 same high resistance to corrosion at room temperature and at te~peratures below Toom temp~rature, particularly in th~ welding zone.
~ or example, for chromium contents o from 22.0 to 24.0~ and moly~denum contents of f~om 3.5 to 4.5%, the nickel cont~nt preferably amounts to between 3,5 and 4.2~. Fo~ chromium contents of ~rom 27.0 ~o 3Q.0% and Mo contents of from 3.7 to 4.2%, the nickel content amounts to between 3.9 and 4.5%.
A preferred composition for a ferritic, stabilised, ch~omium-lQ molybdenum steel includes, by weight p~rcent:
c n. 012~Q,025%
si 0.02 a~s%
Mn ~02~0.5%
c~ 2a.0~22.0%
Ni 3.2_3.5%
Mo 3,a-4,5%
Cu Q~2~0,5%
Ti 0.,2 ~ 4x(C~N2~, but at most Q,7% and/or Nb 0.2 ~ 8x(C~N2), but at most 1.0%
N2 0~005 to 0.015%.
Another pr~ferred composition for a erTitic, stabilised, chromium~ :
moly~denum steel includes, by weight percent:
C 0.012 0.025%
Si 0.02 0,5%
Mn 0~02~0.5%
Cr 24,5~27,0%
Ni 3.5~4~2%
Mo 3,7-4~5~
Cu Q,2~0,S%
30. Ti Q,2 ~ 4x(C~N2~, but at most 0.7% or Nb 0,4 ~ 8x~C~N21, but at most 1~0%
N2 a~o~s.Q~ols%, 3~ :
.
73~ 1 .
In order to demonstrate the surprising and unexpected effect of adding nickel in par~icular to ferrlti~ Cr-Mo steels, the duetillty values determined by notched impact tests are reported in the following with reference to two Examples using steels with the preferred composition according to the invention and, for comparison, conventional steels.
Steels A and C have the composition according to the invention.
EXAMPLE I EXAMPLE II
Steel A Steel B Steel C Steel D ~ ;
C 0.012 0.011 0.014 0.012 `~ `
Si 0.4 0.35 0.41 0.32 Mn 0.32 0.28 0.39 0.33 ; `
Cr 25.7 25.3 21.1 21.2 Ni 4.20 0.10 3.5 0.4 Mo 4.08 3.1 3.2 3.1 `
Ti 0.45 0.41 0.39 0.35 ~-Cu 0.55 0.010 0.38 0.45 Al 0.059 0.049 0.048 0.05 Nb 0.011 0.021 N2 0.015 0.010 0.010 0.0~0 The ductillty v~lues of steels A, B, C and D are shown ~n the orm of graphs ln Figures 1, 2~ 3 and 4, respectively.
The curves "GM" relate to the base material whilst the curves ~'SZ" relate to the zones ad~acent the weld seam which are particularly exposed to the influence of the welding temperature in tenms of embrittlement.
Comparison of the curves "GM" of the two steels A and B shows that the trsn ition temperature of the ~:, steel A according to the invention lie~ between -60~C
and -80C whereas the conventional steel B has a transitio~ temperature which lies between +80C and +100~C.
Comparison of the curves "5Z" shows a transition temperature for the steel A according to the invention of from -40C to -20C and, for the comparison steel B, a transition temperature of from +120~C to ~140C.
The curve "GM" for steel C shows a transition temperature in the range from -30C to -50C. For steel D9 the characteristic values are in the ra~ge from +10C to ~ -+30C. Comparison of ~he curves "SZ" shows a transition temperature for steel C according to the invention of from -10C to + 0C and, for the comparison steel D~ a transition temperature o~ from ~40C to ~50C
So far as the expert is concerned, these results ~ .show that steels, particularly sheet steels, according :~
to the invention in welded constructions do not become `-brittle at room temperature or at temperatures below room temperature. ~ ~ -It is also clear to the expert that the additions of nickel and copper have t~ be selected in such a way that, for optimum ductility, there is little or no reduction in the resistance to stress-corrosion which would be the case for example if additions above th`e upper limits ~or Ni and Cu according to the~invention were to be made, for example 5.0% for Ni and 2.0% for Cu.
The necessary de8ree of invention is embodied in the specified limits of the various alloying ranges, : :
particularly for Ni and Cu. ~:;
So far as the C~N2-content is concerned, it is pointed out that the content ~prescribed in accordance with the invention, namely a relatively high (C~N2)-content , . ~ .
;::
,`-. :
~ 0 ~ 47 3 4 guarantee the reproducibility of the steels which is not the case when the (C~N2)-content is less than 0.015%
and when the objective is for the sum of (C+N2) not to exceed 0~01%~ In addition, reproducibility i~
, facilitated by the nickel content according-to the ;~
invention whereby even fairly large fluctuatiDns in the ~ -C~N2 content have no effect upon the ductility of the steel.
~ ,.
~';
:' .' ' '. ',' .
- ' ~ .
, . ' , ' ~:
` ~ :
` ~
-6- ::
. . .
.
, ~..... .. . .. . . .
Claims (6)
1. Ferritic, stabilised, stainless and corrosion-resistant chromium-molybdenum steels with expressed in weight percent a carbon content of from 0.01 to 0.025%, a nitrogen content of from 0.005 to 0.025%, a chromium content of from 20.0 to 30.0%, a molybdenum content of from 3.0 to 5.0%, manganese and silicon contents of from 0.02 to 1.0% in each case and vanadium, tungsten cobalt and aluminium contents of at most 0.25% in each case, characterised in that they additionally contain nickel in a quantity of from 3.2 to 4.8%, copper in a quantity of from 0.1 to 1.0%, titanium in a quantity of from 0.2 to 0.7% and/or niobium in a quantity of from 0.2 to 1.0%, the rest consisting of iron with the usual impurities, alloying additions of boron and/or zirconium being permitted in quantities which correspond to the prior art.
2. A steel as claimed in Claim 1, characterised in that the sum of the carbon and nitrogen contents amounts to at least 0.015% and to at most 0.04%.
3. A steel as claimed in Claim 1 or 2, characterised in that it has the following chemical composition:
Ti 0.2 + 4x(C+N2), but at most 0.7% and/or Nb 0.2 + 8x(C+N2), but at most 1.0%
N2 0.005 to 0.015%.
Ti 0.2 + 4x(C+N2), but at most 0.7% and/or Nb 0.2 + 8x(C+N2), but at most 1.0%
N2 0.005 to 0.015%.
4. A steel as claimed in Claim 1 or 2, characterised in that, for chromium contents of from 22.0 to 24.0% and molybdenum contents of from 3.5 to 4.5%, the nickel content amounts to between 3.5 and 4.2%.
5. A steel as claimed in Claim 1 or 2, characterised in that, for chromium contents of from 27.0 to 30.0% and Mo contents of from 3.7 to 4.2%, the nickel content amounts to between 3.9 and 4.5%.
6. A steel as claimed in Claim 1 or 2, characterised in that it has the following composition Ti 0.2 + 4x(C+N2), but at most 0.7% or Nb 0.4 + 8x(C+N2), but at most 1.0%
N2 0.005-0.015%.
N2 0.005-0.015%.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DEP2624117.8 | 1976-05-28 | ||
| DE19762624117 DE2624117A1 (en) | 1976-05-28 | 1976-05-28 | TOUGH FERRITIC STEELS AND USE THE SAME FOR METALLIC OBJECTS, IN PARTICULAR WELDED CONSTRUCTIONS |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA1084734A true CA1084734A (en) | 1980-09-02 |
Family
ID=5979295
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA279,345A Expired CA1084734A (en) | 1976-05-28 | 1977-05-27 | Ductile ferritic steels |
Country Status (21)
| Country | Link |
|---|---|
| US (1) | US4216013A (en) |
| JP (1) | JPS5386617A (en) |
| AT (1) | ATA367777A (en) |
| BE (1) | BE855081A (en) |
| BR (1) | BR7703473A (en) |
| CA (1) | CA1084734A (en) |
| CH (1) | CH630414A5 (en) |
| CS (1) | CS203149B2 (en) |
| DE (1) | DE2624117A1 (en) |
| DK (1) | DK234977A (en) |
| ES (1) | ES459221A1 (en) |
| FI (1) | FI67408C (en) |
| FR (1) | FR2352893A1 (en) |
| GB (1) | GB1566204A (en) |
| HU (1) | HU175741B (en) |
| IT (1) | IT1081419B (en) |
| NL (1) | NL7705728A (en) |
| NO (1) | NO149699C (en) |
| PL (1) | PL111236B1 (en) |
| RO (1) | RO74627A (en) |
| SE (1) | SE441103B (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4456482A (en) * | 1980-01-03 | 1984-06-26 | Allegheny Ludlum Steel Corporation | Ferritic stainless steel |
| US4456483A (en) * | 1980-01-03 | 1984-06-26 | Allegheny Ludlum Steel Corporation | Ferritic stainless steel |
| US4374666A (en) * | 1981-02-13 | 1983-02-22 | General Electric Company | Stabilized ferritic stainless steel for preheater and reheater equipment applications |
| CH654594A5 (en) * | 1981-03-16 | 1986-02-28 | Bbc Brown Boveri & Cie | TURBINE BLADE MATERIAL OF HIGH STRENGTH AGAINST CORROSION FATIGUE, METHOD FOR THE PRODUCTION THEREOF AND ITS USE. |
| JPH0717988B2 (en) * | 1991-03-08 | 1995-03-01 | 日本冶金工業株式会社 | Ferritic stainless steel with excellent toughness and corrosion resistance |
| US5393487A (en) * | 1993-08-17 | 1995-02-28 | J & L Specialty Products Corporation | Steel alloy having improved creep strength |
Family Cites Families (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3258370A (en) * | 1964-07-27 | 1966-06-28 | Int Nickel Co | High strength, notch ductile stainless steel products |
| US3677744A (en) * | 1968-03-07 | 1972-07-18 | Suwa Seikosha Kk | Age hardening stainless steel |
| US3837847A (en) * | 1969-07-11 | 1974-09-24 | Int Nickel Co | Corrosion resistant ferritic stainless steel |
| JPS478689U (en) * | 1971-03-01 | 1972-10-02 | ||
| DE2153186A1 (en) * | 1971-10-26 | 1973-05-03 | Deutsche Edelstahlwerke Gmbh | Ferritic chromium steel - used as corrosion-resistant material in chemical appts mfr |
| GB1359629A (en) * | 1971-10-26 | 1974-07-10 | Deutsche Edelstahlwerke Gmbh | Corrosion-resistant ferritic chrome steel |
| ATA285473A (en) * | 1972-04-24 | 1976-09-15 | Bofors Ab | AUSTENITIC-FERRITIC, STAINLESS STEEL WITH HIGH STRENGTH AND GOOD CORROSION RESISTANCE |
| DE2417632A1 (en) * | 1973-04-10 | 1974-11-07 | Daido Steel Co Ltd | Improved ferritic-austenitic stainless steel - combines high proof stress, high corrosion resistance and excellent hot forming properties |
| US4055448A (en) * | 1973-04-10 | 1977-10-25 | Daido Seiko Kabushiki Kaisha | Ferrite-austenite stainless steel |
| JPS568489B2 (en) * | 1974-10-07 | 1981-02-24 | ||
| GB1565419A (en) * | 1976-04-27 | 1980-04-23 | Crucible Inc | Stainless steel welded articles |
-
1976
- 1976-05-28 DE DE19762624117 patent/DE2624117A1/en not_active Ceased
-
1977
- 1977-05-09 SE SE7705336A patent/SE441103B/en not_active IP Right Cessation
- 1977-05-17 GB GB20755/77A patent/GB1566204A/en not_active Expired
- 1977-05-17 IT IT09448/77A patent/IT1081419B/en active
- 1977-05-17 FI FI771566A patent/FI67408C/en not_active IP Right Cessation
- 1977-05-23 AT AT773677A patent/ATA367777A/en not_active Application Discontinuation
- 1977-05-25 JP JP6000277A patent/JPS5386617A/en active Pending
- 1977-05-25 NL NL7705728A patent/NL7705728A/en not_active Application Discontinuation
- 1977-05-25 HU HU77GE1013A patent/HU175741B/en unknown
- 1977-05-26 BE BE177943A patent/BE855081A/en not_active IP Right Cessation
- 1977-05-26 RO RO7790484A patent/RO74627A/en unknown
- 1977-05-27 PL PL1977198448A patent/PL111236B1/en unknown
- 1977-05-27 CH CH659877A patent/CH630414A5/en not_active IP Right Cessation
- 1977-05-27 FR FR7716375A patent/FR2352893A1/en active Granted
- 1977-05-27 ES ES459221A patent/ES459221A1/en not_active Expired
- 1977-05-27 NO NO771873A patent/NO149699C/en unknown
- 1977-05-27 DK DK234977A patent/DK234977A/en not_active Application Discontinuation
- 1977-05-27 BR BR7703473A patent/BR7703473A/en unknown
- 1977-05-27 CS CS773519A patent/CS203149B2/en unknown
- 1977-05-27 CA CA279,345A patent/CA1084734A/en not_active Expired
-
1978
- 1978-09-28 US US05/947,332 patent/US4216013A/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| FI67408B (en) | 1984-11-30 |
| DE2624117A1 (en) | 1977-12-08 |
| IT1081419B (en) | 1985-05-21 |
| HU175741B (en) | 1980-10-28 |
| PL198448A1 (en) | 1978-01-16 |
| SE7705336L (en) | 1977-11-29 |
| US4216013A (en) | 1980-08-05 |
| RO74627A (en) | 1981-04-30 |
| FR2352893B1 (en) | 1978-11-03 |
| FR2352893A1 (en) | 1977-12-23 |
| ES459221A1 (en) | 1978-03-01 |
| SE441103B (en) | 1985-09-09 |
| DK234977A (en) | 1977-11-29 |
| NO771873L (en) | 1977-11-29 |
| JPS5386617A (en) | 1978-07-31 |
| CS203149B2 (en) | 1981-02-27 |
| ATA367777A (en) | 1987-05-15 |
| FI771566A (en) | 1977-11-29 |
| NO149699B (en) | 1984-02-27 |
| CH630414A5 (en) | 1982-06-15 |
| BE855081A (en) | 1977-11-28 |
| GB1566204A (en) | 1980-04-30 |
| FI67408C (en) | 1985-03-11 |
| BR7703473A (en) | 1978-03-14 |
| NO149699C (en) | 1984-06-06 |
| PL111236B1 (en) | 1980-08-30 |
| NL7705728A (en) | 1977-11-30 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| MKEX | Expiry |